JP2019068037A - Semiconductor sintered body, electric/electronic member, and method for manufacturing semiconductor sintered body - Google Patents
Semiconductor sintered body, electric/electronic member, and method for manufacturing semiconductor sintered body Download PDFInfo
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- JP2019068037A JP2019068037A JP2018095172A JP2018095172A JP2019068037A JP 2019068037 A JP2019068037 A JP 2019068037A JP 2018095172 A JP2018095172 A JP 2018095172A JP 2018095172 A JP2018095172 A JP 2018095172A JP 2019068037 A JP2019068037 A JP 2019068037A
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- 239000004065 semiconductor Substances 0.000 title claims abstract description 48
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 238000000034 method Methods 0.000 title description 10
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 53
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 49
- 239000010703 silicon Substances 0.000 claims abstract description 49
- 239000013078 crystal Substances 0.000 claims abstract description 34
- 229910000676 Si alloy Inorganic materials 0.000 claims abstract description 32
- 239000002245 particle Substances 0.000 claims description 95
- 239000002019 doping agent Substances 0.000 claims description 64
- 238000005245 sintering Methods 0.000 claims description 34
- 150000002894 organic compounds Chemical class 0.000 claims description 15
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims description 10
- 239000011574 phosphorus Substances 0.000 claims description 10
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 8
- 229910052796 boron Inorganic materials 0.000 claims description 8
- 229910052797 bismuth Inorganic materials 0.000 claims description 7
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 claims description 7
- GYHNNYVSQQEPJS-UHFFFAOYSA-N Gallium Chemical compound [Ga] GYHNNYVSQQEPJS-UHFFFAOYSA-N 0.000 claims description 6
- 229910052733 gallium Inorganic materials 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052787 antimony Inorganic materials 0.000 claims description 5
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims description 5
- 229910052785 arsenic Inorganic materials 0.000 claims description 5
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims description 5
- 229910052738 indium Inorganic materials 0.000 claims description 5
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 claims description 5
- 229910052716 thallium Inorganic materials 0.000 claims description 5
- BKVIYDNLLOSFOA-UHFFFAOYSA-N thallium Chemical compound [Tl] BKVIYDNLLOSFOA-UHFFFAOYSA-N 0.000 claims description 5
- 230000002708 enhancing effect Effects 0.000 abstract description 3
- 239000011856 silicon-based particle Substances 0.000 description 48
- 238000002360 preparation method Methods 0.000 description 21
- 230000005540 biological transmission Effects 0.000 description 14
- 238000007088 Archimedes method Methods 0.000 description 13
- 239000011248 coating agent Substances 0.000 description 13
- 238000000576 coating method Methods 0.000 description 13
- KFZMGEQAYNKOFK-UHFFFAOYSA-N Isopropanol Chemical compound CC(C)O KFZMGEQAYNKOFK-UHFFFAOYSA-N 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 239000000203 mixture Substances 0.000 description 12
- 239000011324 bead Substances 0.000 description 9
- IMNFDUFMRHMDMM-UHFFFAOYSA-N N-Heptane Chemical compound CCCCCCC IMNFDUFMRHMDMM-UHFFFAOYSA-N 0.000 description 8
- 239000002210 silicon-based material Substances 0.000 description 7
- XYFCBTPGUUZFHI-UHFFFAOYSA-N Phosphine Chemical compound P XYFCBTPGUUZFHI-UHFFFAOYSA-N 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000010248 power generation Methods 0.000 description 6
- ABLZXFCXXLZCGV-UHFFFAOYSA-N Phosphorous acid Chemical compound OP(O)=O ABLZXFCXXLZCGV-UHFFFAOYSA-N 0.000 description 5
- 238000006243 chemical reaction Methods 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 239000002994 raw material Substances 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 4
- 239000002253 acid Substances 0.000 description 4
- 238000005229 chemical vapour deposition Methods 0.000 description 4
- 229910002804 graphite Inorganic materials 0.000 description 4
- 239000010439 graphite Substances 0.000 description 4
- 238000002156 mixing Methods 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 230000000630 rising effect Effects 0.000 description 4
- 239000011863 silicon-based powder Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000000227 grinding Methods 0.000 description 3
- 229910000073 phosphorus hydride Inorganic materials 0.000 description 3
- 229920000642 polymer Polymers 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 2
- BLRPTPMANUNPDV-UHFFFAOYSA-N Silane Chemical compound [SiH4] BLRPTPMANUNPDV-UHFFFAOYSA-N 0.000 description 2
- 229910000577 Silicon-germanium Inorganic materials 0.000 description 2
- LEVVHYCKPQWKOP-UHFFFAOYSA-N [Si].[Ge] Chemical compound [Si].[Ge] LEVVHYCKPQWKOP-UHFFFAOYSA-N 0.000 description 2
- -1 alkyl phosphonic acid Chemical compound 0.000 description 2
- ADCOVFLJGNWWNZ-UHFFFAOYSA-N antimony trioxide Chemical compound O=[Sb]O[Sb]=O ADCOVFLJGNWWNZ-UHFFFAOYSA-N 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 239000012300 argon atmosphere Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- WTEOIRVLGSZEPR-UHFFFAOYSA-N boron trifluoride Chemical compound FB(F)F WTEOIRVLGSZEPR-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 229910052732 germanium Inorganic materials 0.000 description 2
- GNPVGFCGXDBREM-UHFFFAOYSA-N germanium atom Chemical compound [Ge] GNPVGFCGXDBREM-UHFFFAOYSA-N 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- PSCMQHVBLHHWTO-UHFFFAOYSA-K indium(iii) chloride Chemical compound Cl[In](Cl)Cl PSCMQHVBLHHWTO-UHFFFAOYSA-K 0.000 description 2
- 239000005543 nano-size silicon particle Substances 0.000 description 2
- 239000002105 nanoparticle Substances 0.000 description 2
- 239000002002 slurry Substances 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000002904 solvent Substances 0.000 description 2
- 238000002490 spark plasma sintering Methods 0.000 description 2
- TUQOTMZNTHZOKS-UHFFFAOYSA-N tributylphosphine Chemical compound CCCCP(CCCC)CCCC TUQOTMZNTHZOKS-UHFFFAOYSA-N 0.000 description 2
- 229920002554 vinyl polymer Polymers 0.000 description 2
- 229910015900 BF3 Inorganic materials 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910002665 PbTe Inorganic materials 0.000 description 1
- 229910000681 Silicon-tin Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 1
- VSCWAEJMTAWNJL-UHFFFAOYSA-K aluminium trichloride Chemical compound Cl[Al](Cl)Cl VSCWAEJMTAWNJL-UHFFFAOYSA-K 0.000 description 1
- RBFQJDQYXXHULB-UHFFFAOYSA-N arsane Chemical compound [AsH3] RBFQJDQYXXHULB-UHFFFAOYSA-N 0.000 description 1
- UORVGPXVDQYIDP-BJUDXGSMSA-N borane Chemical class [10BH3] UORVGPXVDQYIDP-BJUDXGSMSA-N 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000002109 crystal growth method Methods 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 150000002148 esters Chemical class 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- UPWPDUACHOATKO-UHFFFAOYSA-K gallium trichloride Chemical compound Cl[Ga](Cl)Cl UPWPDUACHOATKO-UHFFFAOYSA-K 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 150000004678 hydrides Chemical class 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052741 iridium Inorganic materials 0.000 description 1
- 150000004715 keto acids Chemical class 0.000 description 1
- LQJIDIOGYJAQMF-UHFFFAOYSA-N lambda2-silanylidenetin Chemical compound [Si].[Sn] LQJIDIOGYJAQMF-UHFFFAOYSA-N 0.000 description 1
- ZGUQQOOKFJPJRS-UHFFFAOYSA-N lead silicon Chemical compound [Si].[Pb] ZGUQQOOKFJPJRS-UHFFFAOYSA-N 0.000 description 1
- 231100001231 less toxic Toxicity 0.000 description 1
- 231100000053 low toxicity Toxicity 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- YACKEPLHDIMKIO-UHFFFAOYSA-N methylphosphonic acid Chemical compound CP(O)(O)=O YACKEPLHDIMKIO-UHFFFAOYSA-N 0.000 description 1
- 238000009768 microwave sintering Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000002086 nanomaterial Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- 229920002959 polymer blend Polymers 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000001272 pressureless sintering Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- OCGWQDWYSQAFTO-UHFFFAOYSA-N tellanylidenelead Chemical compound [Pb]=[Te] OCGWQDWYSQAFTO-UHFFFAOYSA-N 0.000 description 1
- GBECUEIQVRDUKB-UHFFFAOYSA-M thallium monochloride Chemical compound [Tl]Cl GBECUEIQVRDUKB-UHFFFAOYSA-M 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- CMHHITPYCHHOGT-UHFFFAOYSA-N tributylborane Chemical compound CCCCB(CCCC)CCCC CMHHITPYCHHOGT-UHFFFAOYSA-N 0.000 description 1
- AJSTXXYNEIHPMD-UHFFFAOYSA-N triethyl borate Chemical compound CCOB(OCC)OCC AJSTXXYNEIHPMD-UHFFFAOYSA-N 0.000 description 1
- RXJKFRMDXUJTEX-UHFFFAOYSA-N triethylphosphine Chemical compound CCP(CC)CC RXJKFRMDXUJTEX-UHFFFAOYSA-N 0.000 description 1
- JLTRXTDYQLMHGR-UHFFFAOYSA-N trimethylaluminium Chemical compound C[Al](C)C JLTRXTDYQLMHGR-UHFFFAOYSA-N 0.000 description 1
- XCZXGTMEAKBVPV-UHFFFAOYSA-N trimethylgallium Chemical compound C[Ga](C)C XCZXGTMEAKBVPV-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/80—Constructional details
- H10N10/85—Thermoelectric active materials
- H10N10/851—Thermoelectric active materials comprising inorganic compositions
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/80—Constructional details
- H10N10/85—Thermoelectric active materials
- H10N10/851—Thermoelectric active materials comprising inorganic compositions
- H10N10/853—Thermoelectric active materials comprising inorganic compositions comprising arsenic, antimony or bismuth
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B28—WORKING CEMENT, CLAY, OR STONE
- B28B—SHAPING CLAY OR OTHER CERAMIC COMPOSITIONS; SHAPING SLAG; SHAPING MIXTURES CONTAINING CEMENTITIOUS MATERIAL, e.g. PLASTER
- B28B11/00—Apparatus or processes for treating or working the shaped or preshaped articles
- B28B11/24—Apparatus or processes for treating or working the shaped or preshaped articles for curing, setting or hardening
- B28B11/243—Setting, e.g. drying, dehydrating or firing ceramic articles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
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- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B33/00—Silicon; Compounds thereof
- C01B33/06—Metal silicides
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/01—Manufacture or treatment
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/10—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects operating with only the Peltier or Seebeck effects
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/80—Constructional details
- H10N10/85—Thermoelectric active materials
- H10N10/851—Thermoelectric active materials comprising inorganic compositions
- H10N10/855—Thermoelectric active materials comprising inorganic compositions comprising compounds containing boron, carbon, oxygen or nitrogen
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- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/80—Constructional details
- H10N10/85—Thermoelectric active materials
- H10N10/856—Thermoelectric active materials comprising organic compositions
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- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N10/00—Thermoelectric devices comprising a junction of dissimilar materials, i.e. devices exhibiting Seebeck or Peltier effects
- H10N10/80—Constructional details
- H10N10/85—Thermoelectric active materials
- H10N10/857—Thermoelectric active materials comprising compositions changing continuously or discontinuously inside the material
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- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/50—Solid solutions
- C01P2002/52—Solid solutions containing elements as dopants
- C01P2002/54—Solid solutions containing elements as dopants one element only
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- C01—INORGANIC CHEMISTRY
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- C01P2002/00—Crystal-structural characteristics
- C01P2002/60—Compounds characterised by their crystallite size
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- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/01—Particle morphology depicted by an image
- C01P2004/04—Particle morphology depicted by an image obtained by TEM, STEM, STM or AFM
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- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
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- C01P2004/60—Particles characterised by their size
- C01P2004/61—Micrometer sized, i.e. from 1-100 micrometer
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- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
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- C01P2006/32—Thermal properties
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- C—CHEMISTRY; METALLURGY
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- C01P2006/40—Electric properties
Abstract
Description
本発明は、半導体焼結体、電気・電子部材、及び半導体焼結体の製造方法に関する。 The present invention relates to a semiconductor sintered body, an electric / electronic member, and a method of manufacturing the semiconductor sintered body.
半導体は、温度差当たりの起電力(ゼーベック係数)が大きいことから、熱電発電のための熱電材料として有用であることが知られている。その中でも、近年、毒性が低いこと、低コストで入手可能であること、電気的特性の制御が容易であること等から、シリコン系材料に注目が集まっている。 A semiconductor is known to be useful as a thermoelectric material for thermoelectric power generation because of a large electromotive force (seebeck coefficient) per temperature difference. Among them, in recent years, silicon materials have attracted attention because of low toxicity, availability at low cost, easy control of electrical characteristics, and the like.
熱電材料が高い熱電性能を有するためには、材料の電気伝導特率を高く、また熱伝導特率を低くすることが求められる。しかしながら、シリコンの熱伝導率が大きいことから、シリコン系材料の熱電性能は十分であるとはいえなかった。 In order for a thermoelectric material to have high thermoelectric performance, it is required to increase the electrical conductivity of the material and to lower the thermal conductivity. However, due to the high thermal conductivity of silicon, it can not be said that the thermoelectric performance of the silicon-based material is sufficient.
これに対し、近年、ナノサイズのシリコン粒子を焼結すること等によりシリコンをナノ構造化することで、熱伝導率を低下させる技術が知られている(特許文献1、非特許文献1)。 On the other hand, in recent years, there is known a technique for reducing the thermal conductivity by nano-structuring silicon by sintering nano-sized silicon particles or the like (Patent Document 1, Non-patent Document 1).
特許文献1及び非特許文献1に記載されているようなナノ構造化によって、材料の熱伝導率を低下させることができる。しかしながら、ナノ構造化によって電気伝導率も低下してしまうため、シリコン系材料の熱電性能は十分とはいえなかった。 The thermal conductivity of the material can be reduced by nanostructuring as described in US Pat. However, since the electrical conductivity is also lowered due to the nanostructuring, the thermoelectric performance of the silicon-based material is not sufficient.
上記の点に鑑みて、本発明の一形態は、低い熱伝導率を有しつつ、電気伝導率を高めることによって、熱電性能を向上させた半導体材料を提供することを課題とする。 In view of the above-described points, an aspect of the present invention has an object to provide a semiconductor material having improved thermoelectric performance by enhancing the electrical conductivity while having a low thermal conductivity.
本発明の一形態は、多結晶体を含む半導体焼結体であって、前記多結晶体は、シリコン、又はシリコン合金を含み、前記多結晶体を構成する結晶粒の平均粒径が1μm以下であり、電気伝導率が10,000S/m以上である半導体焼結体である。 One embodiment of the present invention is a semiconductor sintered body containing a polycrystalline body, wherein the polycrystalline body contains silicon or a silicon alloy, and the average grain diameter of crystal grains constituting the polycrystalline body is 1 μm or less. It is a semiconductor sintered compact whose electrical conductivity is 10,000 S / m or more.
本発明の一形態によれば、低い熱伝導率を有しつつ、電気伝導率を高めることによって、熱電性能を向上させた半導体材料を提供することができる。 According to one aspect of the present invention, it is possible to provide a semiconductor material with improved thermoelectric performance by enhancing the electrical conductivity while having a low thermal conductivity.
以下、本発明に係る実施形態について、より具体的に説明する。但し、本発明は、ここで取り上げた実施形態に限定されることはなく、発明の技術的思想を逸脱しない範囲で適宜組み合わせや改良が可能である。 Hereinafter, embodiments according to the present invention will be more specifically described. However, the present invention is not limited to the embodiments described here, and appropriate combinations and improvements can be made without departing from the technical concept of the invention.
(半導体焼結体)
本発明の一形態は、多結晶体を含む半導体焼結体であって、多結晶体は、シリコン、又はシリコン合金を含み、多結晶体を構成する結晶粒の平均粒径が1μm以下であり、電気伝導率が10,000S/m以上である半導体焼結体である。また、本発明の一形態による半導体焼結体は、シリコン又はシリコン合金を含む多結晶体であり、多結晶体を構成する結晶粒の平均粒径が1μm以下であり、電気伝導率が10,000S/m以上である。
(Semiconductor sintered body)
One embodiment of the present invention is a semiconductor sintered body containing a polycrystalline body, wherein the polycrystalline body contains silicon or a silicon alloy, and the average grain diameter of crystal grains constituting the polycrystalline body is 1 μm or less. And a semiconductor sintered body having an electrical conductivity of at least 10,000 S / m. The semiconductor sintered body according to one aspect of the present invention is a polycrystalline body containing silicon or a silicon alloy, and the average grain diameter of crystal grains constituting the polycrystalline body is 1 μm or less, and the electric conductivity is 10, It is more than 000 S / m.
熱電材料の熱電性能(熱電変換性能ともいう)を評価する場合、一般に、無次元の熱電性能指数ZT[−]が用いられる。ZTは次式により求められる。
ZT=α2σT/κ ・・・(1)
式(1)中、α[V/K]はゼーベック係数、σ[S/m]は電気伝導率(単位「S/m」中、「S」はジーメンス、「m」はメートル)、κ[W/(mK)]は熱伝導率、Tは絶対温度[K]を表す。ゼーベック係数αは、単位温度差あたりに発生する電位差を指す。また、熱電性能指数ZTが大きいほど、熱電変換性能が優れている。式(1)より明らかなように、熱電変換性能ZTを向上させるためには、ゼーベック係数α及び電気伝導度σが大きく、熱伝導率κが小さいことが望ましい。
In the case of evaluating the thermoelectric performance (also referred to as thermoelectric conversion performance) of the thermoelectric material, generally, a dimensionless thermoelectric performance index ZT [-] is used. ZT is determined by the following equation.
ZT = α 2 σT / κ (1)
In the formula (1), α [V / K] is a Seebeck coefficient, σ [S / m] is an electrical conductivity (in the unit "S / m", "S" is Siemens, "m" is a meter), κ W / (mK)] represents the thermal conductivity, and T represents the absolute temperature [K]. The Seebeck coefficient α indicates the potential difference generated per unit temperature difference. Moreover, the larger the thermoelectric figure of merit ZT, the better the thermoelectric conversion performance. As is clear from the equation (1), in order to improve the thermoelectric conversion performance ZT, it is desirable that the Seebeck coefficient α and the electrical conductivity σ be large and the thermal conductivity 小 さ い be small.
シリコンはゼーベック係数αが高いことが知られており、さらに本形態による上記構成によって、熱伝導率κが低く且つ電気伝導率σが高い半導体焼結体を得ることができるので、結果として、式(1)における熱電性能指数ZTを向上させることができる。また、シリコンは、Bi2Te3やPbTeといった材料に比べ、毒性が小さく、また安価に入手可能である。そのため、本形態による半導体焼結体を用いることで、環境調和型の熱電変換素子(熱電発電素子)、ひいては熱電発電装置を低コストで提供することが可能となる。 Silicon is known to have a high Seebeck coefficient α, and the above configuration according to this embodiment can provide a semiconductor sintered body having a low thermal conductivity 且 つ and a high electrical conductivity σ. The thermoelectric figure of merit ZT in (1) can be improved. In addition, silicon is less toxic than materials such as Bi 2 Te 3 and PbTe, and can be obtained inexpensively. Therefore, by using the semiconductor sintered body according to the present embodiment, it is possible to provide an environment-friendly thermoelectric conversion element (thermoelectric power generation element) and hence a thermoelectric power generation device at low cost.
(多結晶体の構成)
本発明の一形態による半導体焼結体は、シリコンを含む多結晶体である。具体的には、シリコン系多結晶体又はシリコン合金系多結晶体であり、すなわち、主結晶としてシリコン又はシリコン合金を含む多結晶体であることが好ましい。主結晶とは、XRDパターン等において析出割合が最も大きい結晶を指し、好ましくは多結晶体全体のうち55質量%以上を占める結晶を指す。
(Composition of polycrystal)
The semiconductor sintered body according to one aspect of the present invention is a polycrystalline body containing silicon. Specifically, a silicon-based polycrystal or a silicon alloy-based polycrystal, that is, a polycrystal including silicon or a silicon alloy as a main crystal is preferable. The main crystal refers to a crystal having the largest precipitation ratio in an XRD pattern or the like, and preferably refers to a crystal that occupies 55% by mass or more of the entire polycrystal.
半導体焼結体がシリコン合金を含む多結晶体である場合には、シリコンとシリコン以外の元素との固溶体、共晶体、又は金属間化合物であってよい。シリコン合金に含まれる、シリコン以外の元素は、焼結体の低い熱伝導率を維持しつつ電気伝導率を向上させるという本発明の効果を妨げないものであれば特に限定されず、Ge、Fe、Cr、Ta、Nb、Cu、Mn、Mo、W、Ni、Ti、Zr、Hf、Co、Ir、Pt、Ru、Mg、Ba、C、Sn等が挙げられる。これらは、シリコン合金中に1種又は2種以上含まれていてよい。また、シリコン合金としては、1種又は2種以上の上記のシリコン以外の元素を2〜20質量%で含有するものが好ましい。また、シリコン合金としては、シリコン−ゲルマニウム合金、シリコン−スズ合金、シリコン−鉛合金が好ましい。中でも、熱伝導率を下げる観点から、シリコン−ゲルマニウム合金がより好ましい。 When the semiconductor sintered body is a polycrystalline body containing a silicon alloy, it may be a solid solution of silicon and an element other than silicon, a eutectic, or an intermetallic compound. Elements other than silicon contained in the silicon alloy are not particularly limited as long as they do not impair the effect of the present invention of improving the electrical conductivity while maintaining the low thermal conductivity of the sintered body, and Ge, Fe And Cr, Ta, Nb, Cu, Mn, Mo, W, Ni, Ti, Zr, Hf, Co, Ir, Pt, Ru, Mg, Ba, C, Sn and the like. One or more of these may be contained in the silicon alloy. Moreover, as a silicon alloy, what contains 2 to 20 mass% of elements other than said 1 type or 2 types of above-mentioned silicons is preferable. Moreover, as a silicon alloy, a silicon-germanium alloy, a silicon-tin alloy, and a silicon-lead alloy are preferable. Among them, a silicon-germanium alloy is more preferable from the viewpoint of lowering the thermal conductivity.
半導体焼結体は、多結晶体を構成する結晶粒の平均粒径が1μm以下である、いわゆるナノ構造を有する多結晶体である。また、結晶粒の平均粒径は、1μm未満であると好ましく、800nm以下であるとより好ましく、500nm以下であるとさらに好ましく、300nm以下であるとさらに好ましく、150nm以下であるとさらに好ましい。結晶粒の粒径を上記範囲とすることで、結晶粒の大きさが、多結晶体におけるフォノンの平均自由行程より十分小さくなるので、界面でのフォノン散乱により熱伝導率を低下させることが可能となる。 The semiconductor sintered body is a polycrystalline body having a so-called nano structure in which the average grain size of crystal grains constituting the polycrystalline body is 1 μm or less. The average grain size of the crystal grains is preferably less than 1 μm, more preferably 800 nm or less, still more preferably 500 nm or less, still more preferably 300 nm or less, and still more preferably 150 nm or less. By setting the grain size of the crystal grains in the above range, the size of the crystal grains is sufficiently smaller than the mean free path of phonons in a polycrystal, so that the thermal conductivity can be reduced by phonon scattering at the interface. It becomes.
また、結晶粒の平均粒径の下限は、特に限定されないが、製造上の制約から1nm以上とすることができる。 Further, the lower limit of the average grain size of the crystal grains is not particularly limited, but can be 1 nm or more in view of manufacturing limitations.
なお、本明細書において、結晶粒の平均粒径とは、走査型電子顕微鏡(Scaning Electron Microscope(SEM))や透過型電子顕微鏡(Transmission Electron Microscope(TEM))等の顕微鏡で直接観察して測定した、結晶体を構成する個々の結晶粒の最も長い径のメジアン値をいう。 In the present specification, the average grain diameter of crystal grains is measured by direct observation with a microscope such as a scanning electron microscope (SEM) or a transmission electron microscope (TEM). Refers to the median value of the longest diameter of the individual crystal grains that make up the crystal.
半導体焼結体の電気伝導率は、10,000S/m以上であり、50,000S/mであることが好ましく、90,000S/m以上であることが好ましく、100,000S/m以上であるとより好ましく、110,000S/m以上であるとさらに好ましい。上記電気伝導率は、27℃における値とすることができる。このように、向上させた電気伝導率を有することで、熱電性能を向上させることができる。また、半導体焼結体の電気伝導率の上限は、27℃において600,000S/m以下とすることができ、400,000S/m以下とすることができる。熱電性能ZTは、例えば527℃で0.2以上にすることができ、好ましくは0.3以上、さらに0.4以上にすることができる。 The electrical conductivity of the semiconductor sintered body is 10,000 S / m or more, preferably 50,000 S / m, preferably 90,000 S / m or more, and 100,000 S / m or more. And more preferably 110,000 S / m or more. The said electrical conductivity can be made into the value in 27 degreeC. Thus, thermoelectric performance can be improved by having the improved electrical conductivity. In addition, the upper limit of the electrical conductivity of the semiconductor sintered body can be 600,000 S / m or less at 27 ° C., and can be 400,000 S / m or less. The thermoelectric performance ZT can be, for example, 0.2 or more at 527 ° C., preferably 0.3 or more, and further preferably 0.4 or more.
本形態による半導体焼結体の熱伝導率は、25W/m・K以下であると好ましく、10W/m・K以下であるとより好ましい。上記熱伝導率は、27℃における値とすることができる。また、半導体焼結体のゼーベック係数の絶対値は、50〜150μV/Kであると好ましく、80〜120μV/Kであるとより好ましい。上記値は、27℃における値とすることができる。 The thermal conductivity of the semiconductor sintered body according to the present embodiment is preferably 25 W / m · K or less, and more preferably 10 W / m · K or less. The said thermal conductivity can be made into the value in 27 degreeC. The absolute value of the Seebeck coefficient of the semiconductor sintered body is preferably 50 to 150 μV / K, and more preferably 80 to 120 μV / K. The above value can be a value at 27 ° C.
(ドーパント)
本形態の半導体焼結体は、用途に応じて、n型又はp型のドーパントを含むことができる。ドーパントは、焼結体全体にわたり均一に分散していることが好ましい。n型のドーパントとしては、リン、ヒ素、アンチモン、ビスマスのうち1種を単独で又は2種以上を併せて含有していることが好ましい。また、p型のドーパントとしては、ホウ素、アルミニウム、ガリウム、インジウム、タリウムのうち1種を単独で又は2種以上を併せて含有していることが好ましい。なお、上記ドーパント元素の導電型は例示であり、ドーパント元素がn型及びp型のいずれの型のドーパントとして機能するかは、得られる焼結体における母結晶を構成する元素の種類、結晶の構造等によって異なる。
(Dopant)
The semiconductor sintered body of the present embodiment can contain an n-type or p-type dopant depending on the application. The dopant is preferably dispersed uniformly throughout the sintered body. As the n-type dopant, it is preferable to contain one of phosphorus, arsenic, antimony and bismuth singly or in combination of two or more. Further, as the p-type dopant, it is preferable to contain one of boron, aluminum, gallium, indium and thallium singly or in combination of two or more. The conductivity type of the above dopant element is an example, and whether the dopant element functions as a dopant of either n-type or p-type depends on the type of the element constituting the mother crystal in the obtained sintered body and the crystal. It depends on the structure etc.
焼結体中のドーパント濃度は、n型ドーパントの場合には、[1020原子数/cm3]を単位として0.1〜10であると好ましく、0.5〜5であるとより好ましい。また、焼結体中のドーパント濃度は、p型ドーパントの場合、[1020原子数/cm3]を単位として0.1〜10であると好ましく、0.5〜5であるとより好ましい。ドーパント濃度を大きくすることで電気伝導率を向上させることができるので熱電性能ZTは向上するものの、ドーパント濃度が過度に大きくなるとゼーベック係数が低下しかつ熱伝導率が増大するため、熱電性能ZTは低下してしまう。しかし、ドーパント濃度を上記範囲とすることで、熱電性能ZTを向上させることができる。 In the case of an n-type dopant, the dopant concentration in the sintered body is preferably 0.1 to 10 and more preferably 0.5 to 5 in a unit of [10 20 atoms / cm 3 ]. In the case of a p-type dopant, the dopant concentration in the sintered body is preferably 0.1 to 10 and more preferably 0.5 to 5 in a unit of [10 20 atoms / cm 3 ]. Since the electrical conductivity can be improved by increasing the dopant concentration, the thermoelectric performance ZT improves, but if the dopant concentration becomes excessively large, the Seebeck coefficient decreases and the thermal conductivity increases, so the thermoelectric performance ZT is It will decrease. However, by setting the dopant concentration in the above range, the thermoelectric performance ZT can be improved.
また、n型ドーパントは、半導体焼結体のゼーベック係数が−185〜−60μV/Kとなる濃度で含有されていると好ましく、p型ドーパントは、半導体焼結体のゼーベック係数が60〜185μV/Kとなる濃度で含有されていると好ましい。 The n-type dopant is preferably contained at a concentration such that the Seebeck coefficient of the semiconductor sintered body is −185 to −60 μV / K, and the p-type dopant has a Seebeck coefficient of 60 to 185 μV / of the semiconductor sintered body. It is preferable to be contained at a concentration that gives K.
(電気・電子部材)
上述のように、本形態によれば、低い熱伝導率を維持しつつ、電気伝導率を高めた半導体焼結体を得ることができる。そのため、電気・電子部材、特に、熱電素子として用いることができる。中でも、排熱を利用した発電装置、例えば、自動車や船舶等の発動機および排気系に装着される発電装置、工業的に利用される加熱炉の放熱系に装着される発電装置等において好適に用いることができる。
(Electric and electronic components)
As described above, according to the present embodiment, it is possible to obtain a semiconductor sintered body with high electrical conductivity while maintaining low thermal conductivity. Therefore, it can be used as an electric / electronic member, in particular, a thermoelectric element. Among them, power generation devices utilizing exhaust heat, for example, power generation devices mounted on engines and exhaust systems such as automobiles and ships, power generation devices mounted on heat dissipation systems of heating furnaces used industrially, etc. It can be used.
(半導体焼結体の製造方法)
本形態による半導体焼結体の製造方法は、シリコン又はシリコン合金を含み平均粒径が1μm以下である粒子を準備する粒子準備ステップと、粒子の表面に、ドーパント元素を含む有機化合物の被膜を形成する被膜形成ステップと、被膜が表面に形成された粒子を焼結して、半導体焼結体を得る焼結ステップとを含む。
(Method of manufacturing semiconductor sintered body)
In the method for producing a semiconductor sintered body according to the present embodiment, a particle preparing step of preparing particles containing silicon or a silicon alloy and having an average particle diameter of 1 μm or less, and a film of an organic compound containing a dopant element on the surface of the particles. Forming a film, and sintering the particles having the film formed on the surface to obtain a semiconductor sintered body.
シリコン又はシリコン合金を含み平均粒径が1μm以下である粒子を準備する粒子準備ステップでは、例えば、主結晶となるシリコン又はシリコン合金の材料を溶融し、冷却して得られる固体を、公知の粉砕方法により粉砕することにより、平均粒径1μm以下の粒子(粉末)を準備することができる。また、化学気相成長法(CVD)等の公知の結晶成長法を用いて、シリコン又はシリコン合金の原料から粒子(粉末)を合成することができる。 In the particle preparation step of preparing particles containing silicon or silicon alloy and having an average particle diameter of 1 μm or less, for example, a solid obtained by melting and cooling a material of silicon or silicon alloy as a main crystal is known grinding. By pulverizing according to a method, particles (powder) having an average particle diameter of 1 μm or less can be prepared. In addition, particles (powder) can be synthesized from a raw material of silicon or silicon alloy by using a known crystal growth method such as chemical vapor deposition (CVD).
粒子準備ステップにおいて得られる粒子の平均粒径は、1μm未満であると好ましく、800nmであるとより好ましく、500nmであるとさらに好ましく、300nmであるとさらに好ましい。また、粒子のD90が、1μm以下であると好ましく、500nm以下であるとより好ましく、200nm以下であるとさらに好ましい。焼結前の粒子の粒径を上記範囲とすることで、1μm以下の粒径の結晶粒を有し、且つ適度に緻密化された焼結体を得ることができる。なお、粒子準備ステップにおいて準備する粒子の平均粒径の下限は限定されないが、製造上の制約から10nm以上とすることが好ましい。なお、本明細書において、粒子の平均粒径とは、レーザ回折式粒度分布測定装置により測定した体積基準のメジアン径とすることができる。 The average particle diameter of the particles obtained in the particle preparation step is preferably less than 1 μm, more preferably 800 nm, still more preferably 500 nm, and still more preferably 300 nm. In addition, D90 of the particles is preferably 1 μm or less, more preferably 500 nm or less, and still more preferably 200 nm or less. By setting the particle size of the particles before sintering to the above range, it is possible to obtain a sintered body having crystal grains with a particle size of 1 μm or less and appropriately densified. The lower limit of the average particle diameter of the particles prepared in the particle preparation step is not limited, but is preferably 10 nm or more in view of production limitations. In the present specification, the average particle diameter of particles may be a volume-based median diameter measured by a laser diffraction type particle size distribution measuring device.
続いて、上記の粒子準備ステップで得られた粒子の表面に、ドーパント元素を含む有機化合物の被膜を形成する被膜形成ステップを行う。この被膜形成ステップは、粒子準備ステップで得られた粒子を溶媒に分散させた後、上記のドーパント元素を含む有機化合物を混合して、ビーズミル等で混合処理することによって行うことができる。なお、ドーパント元素を含む有機化合物は、混合物の形態として粒子の分散体に加えてもよい。その後、減圧等によって溶媒を除去し、乾燥することによって、ドーパント元素を含む有機化合物の被膜が表面に形成された粒子を得ることができる。この場合、被膜の厚さは0.5〜5nmであってよく、有機化合物の単分子膜であることが好ましい。 Subsequently, a film forming step of forming a film of an organic compound containing a dopant element on the surface of the particles obtained in the above particle preparation step is performed. This film formation step can be carried out by dispersing the particles obtained in the particle preparation step in a solvent, mixing the organic compounds containing the above-mentioned dopant element, and mixing treatment in a bead mill or the like. The organic compound containing the dopant element may be added to the particle dispersion in the form of a mixture. Thereafter, the solvent is removed by reduced pressure or the like, and the particles are dried to obtain particles in which a film of an organic compound containing a dopant element is formed on the surface. In this case, the thickness of the film may be 0.5 to 5 nm, and is preferably a monomolecular film of an organic compound.
有機化合物に含有させるドーパント元素は、用途に応じて、n型又はp型の上述のドーパント元素を用いることができる。n型のドーパント元素としては、リン、ヒ素、アンチモン、ビスマスのうち1種又は2種以上とすることができる。p型のドーパント元素としては、ホウ素、アルミニウム、ガリウム、インジウム、タリウムのうち1種又は2種以上とすることができる。 As the dopant element contained in the organic compound, the above-described dopant element of n-type or p-type can be used depending on the application. The n-type dopant element may be one or more of phosphorus, arsenic, antimony and bismuth. The p-type dopant element can be one or more of boron, aluminum, gallium, indium and thallium.
また、ドーパント元素を含む有機化合物は、高分子であっても低分子であってもよい。有機化合物としては、ドーパント元素を含む水素化物、酸化物、オキソ酸等であってよい。 The organic compound containing the dopant element may be a polymer or a low molecule. The organic compound may be a hydride containing a dopant element, an oxide, an oxo acid or the like.
n型ドーパント元素としてリンを用いる場合、有機化合物としては、リン酸、アルキルホスホン酸、アルキルホスフィン酸及びそのエステル、ポリビニルホスホン酸、ホスフィン、トリエチルホスフィン、トリブチルホスフィン等のトリアルキルホスフィン等を用いることができる。また、ホスホン酸を含むポリマー(ホスホン酸ポリマー)を用いてもよい。ドーパント元素としてヒ素を用いる場合には、アルシン等を用いることができ、アンチモンを用いる場合には三酸化アンチモン等を用いることができ、ビスマスを用いる場合には、ビスマス酸を用いることができる。 When phosphorus is used as the n-type dopant element, as the organic compound, phosphoric acid, alkyl phosphonic acid, alkyl phosphinic acid and esters thereof, polyvinyl phosphonic acid, trialkyl phosphine such as phosphine, triethyl phosphine, tributyl phosphine, etc. may be used. it can. Alternatively, a polymer containing phosphonic acid (phosphonic acid polymer) may be used. When arsenic is used as the dopant element, arsine or the like can be used, antimony trioxide can be used when antimony is used, and bismuth acid can be used when bismuth is used.
p型ドーパント元素としてホウ素を用いる場合には、有機化合物として、デカボラン、オルトデカボラン等のボランクラスターや、三フッ化ホウ素等を用いることができる。また、ドーパント元素としてアルミニウムを用いる場合には、三塩化アルミニウム、トリメチルアルミニウム等を用いることができ、ガリウムを用いる場合には三塩化ガリウム、トリメチルガリウム等を用いることができ、インジウムを用いる場合には三塩化インジウム等を用いることができ、タリウムを用いる場合には塩化タリウム等を用いることができる。上記有機化合物は、単独で又は2種以上を併せて使用することができる。 When boron is used as the p-type dopant element, borane clusters such as decaborane and ortho decaborane, boron trifluoride and the like can be used as the organic compound. When aluminum is used as the dopant element, aluminum trichloride, trimethylaluminum or the like can be used. When gallium is used, gallium trichloride, trimethylgallium or the like can be used. When indium is used. Indium trichloride or the like can be used, and when thallium is used, thallium chloride or the like can be used. The above organic compounds can be used alone or in combination of two or more.
被膜形成ステップにおいては、ドーパント元素を含む有機化合物を、粒子準備ステップで準備された粒子100質量部に対して、3〜60質量部で添加することが好ましく、10〜30質量部で添加することがより好ましい。 In the film forming step, the organic compound containing the dopant element is preferably added in an amount of 3 to 60 parts by mass, preferably 10 to 30 parts by mass, with respect to 100 parts by mass of the particles prepared in the particle preparation step. Is more preferred.
焼結ステップは、上述の原料粒子(粉末)を焼結することのできる方法であれば、特に限定されないが、放電プラズマ焼結法(Spark Plasma Sintering(SPS))、常圧焼結法(Two Step Sintering)、加圧焼結法(Hot Pressing)、熱間等方加圧焼結法(Hot Isostatic Pressing(HIP))、マイクロ波焼結法(Microwave Sintering)等が挙げられる。これらのうち、より小さい結晶粒を得ることのできる放電プラズマ焼結法を用いることが好ましい。 The sintering step is not particularly limited as long as it is a method capable of sintering the above-mentioned raw material particles (powder), but a spark plasma sintering method (Spark Plasma Sintering (SPS)), a pressureless sintering method (Two) Step Sintering, Hot Pressing, Hot Isostatic Pressing (HIP), Microwave Sintering, etc. may be mentioned. Among these, it is preferable to use a discharge plasma sintering method capable of obtaining smaller crystal grains.
焼結ステップにおける焼結温度は、シリコン又はシリコン合金である主結晶の組成に応じて選択することができるが、900℃以上であると好ましく、1000℃以上であるとより好ましい。また、焼結温度は、1400℃以下であると好ましく、1300℃以下であるとより好ましい。上記範囲とすることで、焼結体の緻密化を促進し、また多結晶体の結晶粒の平均粒径を1μm以下に維持することができる。 The sintering temperature in the sintering step can be selected according to the composition of the main crystal that is silicon or silicon alloy, but is preferably 900 ° C. or more, and more preferably 1000 ° C. or more. The sintering temperature is preferably 1400 ° C. or less, more preferably 1300 ° C. or less. By setting it as the said range, densification of a sintered compact can be accelerated | stimulated and the average particle diameter of the crystal grain of a polycrystal can be maintained at 1 micrometer or less.
また、焼結ステップにおける昇温速度は、10〜100℃/分であると好ましく、20〜60℃/分であるとより好ましい。昇温速度を上記範囲とすることで、均一な焼結を促進すると共に、過度に急速な粒成長を抑制して多結晶体の結晶粒の平均粒径を1μm以下に維持することができる。 Moreover, the temperature rising rate in the sintering step is preferably 10 to 100 ° C./min, and more preferably 20 to 60 ° C./min. By setting the temperature rising rate to the above range, uniform sintering can be promoted, and excessively rapid grain growth can be suppressed to maintain the average grain size of the polycrystalline grains at 1 μm or less.
焼結ステップにおいては、加圧されていることが好ましい。その場合、加圧圧力は、10〜120MPaであると好ましく、30〜100MPaであるとより好ましい。 In the sintering step, pressure is preferably applied. In that case, the applied pressure is preferably 10 to 120 MPa, and more preferably 30 to 100 MPa.
また、本形態は、シリコン又はシリコン合金を含み平均粒径が1μm以下である粒子を準備し、粒子の表面に、ドーパント元素を含む有機化合物の被膜を形成し、被膜が表面に形成された粒子を焼結して、半導体焼結体を得ることによって製造された半導体焼結体である。このような半導体焼結体は、低い熱導電率を維持しながらも、高い電気伝導率を有している。そのため、高い熱電性能ZTを有する半導体焼結体を提供することができる。 In addition, in this embodiment, particles containing silicon or silicon alloy and having an average particle diameter of 1 μm or less are prepared, a film of an organic compound containing a dopant element is formed on the surface of the particles, and particles are formed on the surface And sintered to obtain a semiconductor sintered body. Such a semiconductor sintered body has high electrical conductivity while maintaining low thermal conductivity. Thus, a semiconductor sintered body having high thermoelectric performance ZT can be provided.
上記のように、表面にドーパント元素を含む被膜を形成した粒子を焼結すると、焼結時には、粒子の界面から粒子の内部へとドーピング元素が熱拡散する。このような粒子界面からの熱拡散によるドーピングによって、結果として得られる焼結体の電気伝導率を向上させることができる。また、本形態による方法で得られた半導体焼結体は、同等のドーパント濃度を有するが粒子界面からの熱拡散を利用せずにドープされた焼結体と比較した場合であっても、より高い電気伝導率を示し得る。 As described above, when the particles in which the film containing the dopant element is formed on the surface are sintered, the doping element is thermally diffused from the interface of the particles to the inside of the particles during sintering. Such doping by thermal diffusion from the particle interface can improve the electrical conductivity of the resulting sintered body. In addition, the semiconductor sintered body obtained by the method according to the present embodiment has a comparable dopant concentration, but it is better compared to a sintered body that is doped without using thermal diffusion from the particle interface. It can exhibit high electrical conductivity.
なお、上述のように、本形態による方法では、被膜形成ステップにおいて被膜にドーパント元素を含有させ、焼結ステップにおいて粒子界面からの熱拡散させることによってドーピングを行っている。しかし、粒子準備ステップの段階で予め粒子内にドーパントを含有させておいた上で、上述の被膜形成ステップを行うことができる。例えば、主結晶となるシリコン又はシリコン合金の材料を溶融する段階で、ドーパント元素単体又はその化合物を混合し、得られた溶融物を冷却、粉砕することによって、ドーパントを含む粒子(粉末)を準備することができる。また、化学気相成長法(CVD)等を用いて粒子を準備する場合には、シリコン又はシリコン合金の原料と、ドーパント元素の単体又は化合物とを気相状態で混合し、凝結させて、ドーパントを含む粒子を準備することができる。 As described above, in the method according to the present embodiment, doping is performed by causing the film to contain the dopant element in the film forming step, and thermally diffusing from the particle interface in the sintering step. However, it is possible to carry out the above-mentioned film formation step after the dopant is previously contained in the particles at the stage of the particle preparation step. For example, at the stage of melting the material of silicon or silicon alloy as the main crystal, the dopant element alone or its compound is mixed, and the resulting melt is cooled and crushed to prepare particles (powder) containing the dopant. can do. Moreover, when preparing particles using chemical vapor deposition (CVD) or the like, the raw material of silicon or silicon alloy and the simple substance or compound of the dopant element are mixed in the vapor state and condensed to obtain the dopant. The particles can be prepared.
このように、粒子準備ステップの段階でドーパントを含有させた上、被膜形成ステップ及び焼成ステップによって粒子表面から粒子内へとドーパントをさらに熱拡散させることによって、より高濃度のドーピングが可能となる。 Thus, doping can be made higher by incorporating the dopant at the stage of the particle preparation step and further thermally diffusing the dopant from the particle surface into the particle by the film forming step and the baking step.
[n型半導体焼結体]
<実施例1>
(シリコン粒子の調製)
単体シリコン(純度99.99%以上)28g、及び単体リン(純度99.9%)1.0gを、アーク溶解装置によりアルゴン雰囲気下で融解し、その後冷却した。冷却により得られた塊状物を転動して再び融解して冷却した。この融解及び冷却を計4サイクル繰り返し、母材となるドーパント入りシリコン材を得た。このシリコン材を、ハンマークラッシャー及び遊星ボールミルを利用して、45μm以下に粗粉砕した。さらに、ビーズミルを用いてD90が150nm程度となるまで粉砕した。このとき、媒体としてイソプロピルアルコールを用い、ビーズとして0.05mm径のジルコニアビーズを使用した。得られたスラリーからイソプロピルアルコールを減圧して除去し、さらに乾燥してシリコン粒子を得た。
[N-type semiconductor sintered body]
Example 1
(Preparation of silicon particles)
28 g of elemental silicon (purity 99.99% or more) and 1.0 g of elemental phosphorus (purity 99.9%) were melted by an arc melting apparatus under an argon atmosphere, and then cooled. The mass obtained by cooling was rolled again to melt and cool. The melting and cooling were repeated a total of four cycles to obtain a dopant-containing silicon material as a base material. This silicon material was roughly crushed to 45 μm or less using a hammer crusher and a planetary ball mill. Furthermore, it grind | pulverized until D90 becomes about 150 nm using the bead mill. At this time, isopropyl alcohol was used as a medium, and zirconia beads of 0.05 mm in diameter were used as beads. From the resulting slurry, isopropyl alcohol was removed under reduced pressure and further dried to obtain silicon particles.
(粒子の被覆)
得られたシリコン粒子をヘプタンに分散し、シリコン粒子5.0gに対してポリビニルホスホン酸(シグマアルドリッチ社製)1.0gを加えた混合物を上記のビーズミルに投入し、混合処理を300分間行った。その後、ヘプタンを減圧除去し、さらに乾燥して単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
The obtained silicon particles were dispersed in heptane, and a mixture prepared by adding 1.0 g of polyvinylphosphonic acid (manufactured by Sigma-Aldrich Co.) to 5.0 g of silicon particles was charged into the above-described bead mill, and the mixing treatment was performed for 300 minutes. . Thereafter, heptane was removed under reduced pressure and further dried to obtain monomolecular film-coated silicon particles.
(焼結)
上記単分子膜被覆が施されたシリコン粒子を、黒鉛製のダイ/パンチ冶具内に装入して、放電プラズマ焼結装置を用いて1200℃まで昇温し、焼結体を得た。このとき、加圧圧力を80MPaとし、また昇温速度を50℃/分として行った。得られた焼結体の外表面を粗研磨して黒鉛等に由来する不純物層を除去した。さらにダイシングソーを使用して切断し、直方体状のチップを得た。
(Sintering)
The silicon particles coated with the monomolecular film were loaded into a die / punch jig made of graphite, and heated to 1200 ° C. using a discharge plasma sintering apparatus to obtain a sintered body. At this time, the pressurizing pressure was 80 MPa, and the temperature rising rate was 50 ° C./min. The outer surface of the obtained sintered body was roughly polished to remove an impurity layer derived from graphite or the like. Furthermore, it cut | disconnected using the dicing saw and obtained the cube-shaped chip | tip.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.1×105S/mであり、熱伝導率は、10.5W/m・Kであった。焼結体のゼーベック係数(−89.2μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.30であった。 The electric conductivity at 27 ° C. of the sintered body was 1.1 × 10 5 S / m, and the thermal conductivity was 10.5 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (-89.2 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.30.
<実施例2>
(シリコン粒子の調製)
実施例1と同様に、シリコン粒子を調製した。
Example 2
(Preparation of silicon particles)
As in Example 1, silicon particles were prepared.
(粒子の被覆)
ポリビニルホスホン酸1.0gに代えてトリブチルホスフィン1.6gを加えた混合物を用いたこと以外は、実施例1と同様にして単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
A monomolecular film-coated silicon particle was obtained in the same manner as in Example 1 except that a mixture in which 1.6 g of tributylphosphine was added instead of 1.0 g of polyvinylphosphonic acid was used.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 1, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and furthermore, a rectangular chip was obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. In addition, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon particles having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.0×105S/mであり、熱伝導率は、10.0W/m・Kであった。焼結体のゼーベック係数(−94.9μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.1であった。また、527℃における熱電性能指数ZTは0.29であった The electric conductivity at 27 ° C. of the sintered body was 1.0 × 10 5 S / m, and the thermal conductivity was 10.0 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (−94.9 μV / K) of the sintered body, and was 2.1 based on [10 20 atoms / cm 3 ]. Also, the thermoelectric figure of merit ZT at 527 ° C. was 0.29
<実施例3>
(シリコン粒子の調製)
実施例1と同様にして、シリコン粒子を調製した。
Example 3
(Preparation of silicon particles)
Silicon particles were prepared as in Example 1.
(粒子の被覆)
ポリビニルホスホン酸1.0gに代えてメチルホスホン酸1.0gを加えた混合物を用いたこと以外は実施例1と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
A monomolecular film-coated silicon particle was obtained in the same manner as in Example 1 except that a mixture in which 1.0 g of methylphosphonic acid was added instead of 1.0 g of polyvinylphosphonic acid was used.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 1, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and furthermore, a rectangular chip was obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.1×105S/mであり、熱伝導率は、10.5W/m・Kであった。焼結体のゼーベック係数(−91.0μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.30であった。 The electric conductivity at 27 ° C. of the sintered body was 1.1 × 10 5 S / m, and the thermal conductivity was 10.5 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (-91.0 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.30.
<実施例3A>
(シリコン粒子の調製)
実施例1と同様にして、シリコン粒子を調製した。
Example 3A
(Preparation of silicon particles)
Silicon particles were prepared as in Example 1.
(粒子の被覆)
ポリビニルホスホン酸1.0gに代えてホスホン酸ポリマー混合物(リン含有率22wt%、日東電工(株)開発品、No.DB81)1.1gを加えた混合物を用いたこと以外は実施例1と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
The same as Example 1 except that a mixture obtained by adding 1.1 g of a phosphonic acid polymer mixture (phosphorus content 22 wt%, Nitto Denko Corp. developed product, No. DB 81) in place of 1.0 g of polyvinyl phosphonic acid was used. Thus, silicon particles coated with a monomolecular film were obtained.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 1, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and furthermore, a rectangular chip was obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.2×105S/mであり、熱伝導率は、10.0W/m・Kであった。焼結体のゼーベック係数(−90.1μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.31であった。 The electric conductivity at 27 ° C. of the sintered body was 1.2 × 10 5 S / m, and the thermal conductivity was 10.0 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (−90.1 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.31.
<実施例4>
(シリコン粒子の調製)
単体リン(純度99.9%)1.0gに代えて、単体リン(純度99.9%)0.5g及び単体ビスマス(純度99.99%以上)3.5gを用いたこと以外は実施例1と同様にして、シリコン粒子を得た。
Example 4
(Preparation of silicon particles)
Example except that 0.5 g of single phosphorus (purity 99.9%) and 3.5 g of single bismuth (purity 99.99% or higher) were used instead of 1.0 g of single phosphorus (purity 99.9%) Silicon particles were obtained in the same manner as in 1.
(粒子の被覆)
実施例1と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
In the same manner as in Example 1, silicon particles coated with a monomolecular film were obtained.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Sintering)
In the same manner as in Example 1, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and furthermore, a rectangular chip was obtained.
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.2×105S/mであり、熱伝導率は、9.0W/m・Kであった。焼結体のゼーベック係数(−93.5μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.1であった。また、527℃における熱電性能指数ZTは0.40であった。 The electrical conductivity at 27 ° C. of the sintered body was 1.2 × 10 5 S / m, and the thermal conductivity was 9.0 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (−93.5 μV / K) of the sintered body, and was 2.1 based on [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.40.
<実施例5>
(シリコン粒子の調製)
モノシラン(SiH4、純度99.9%)100モル当量、及びホスフィン(PH3、純度99.9%)3モル当量を原料とし、アルゴン/水素混合気を通じてマイクロ波プラズマ反応器により反応させてナノ粒子を合成し、インラインフィルタで捕集した。シリコンナノ粒子が、平均粒径150nm程度の凝集体として得られ、その結晶子の平均径は10nmであった。
Example 5
(Preparation of silicon particles)
Using 100 molar equivalents of monosilane (SiH 4 , purity 99.9%) and 3 molar equivalents of phosphine (PH 3 , purity 99.9%) as raw materials, reaction is performed by a microwave plasma reactor through an argon / hydrogen mixture. The particles were synthesized and collected by an in-line filter. Silicon nanoparticles were obtained as an aggregate having an average particle diameter of about 150 nm, and the average diameter of the crystallites was 10 nm.
(粒子の被覆)
実施例1と同様に処理して、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
The same treatment as in Example 1 was carried out to obtain monomolecular film-coated silicon particles.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 1, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and furthermore, a rectangular chip was obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は0.9×105S/mであり、熱伝導率は、8.4W/m・Kであった。焼結体のゼーベック係数(−95.0μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.0であった。また、527℃における熱電性能指数ZTは0.50であった。 The electric conductivity at 27 ° C. of the sintered body was 0.9 × 10 5 S / m, and the thermal conductivity was 8.4 W / m · K. When the dopant concentration was calculated based on the Seebeck coefficient (-95.0 μV / K) of the sintered body, it was 2.0 in units of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.50.
<実施例6>
(シリコン合金粒子の調製)
単体シリコン(純度99.99%以上)28gに代えて、単体シリコン(純度99.99%以上)28g及び単体ゲルマニウム(純度99.99%以上)3.0gを用い、単体リン(純度99.9%)の量を0.5gに変更したこと以外は実施例1と同様にして粒子を調製し、シリコン合金粒子を得た。
Example 6
(Preparation of silicon alloy particles)
28 g of single silicon (purity 99.99% or higher), 28 g of single silicon (purity 99.99% or higher) and 3.0 g of single germanium (purity 99.99% or higher), single phosphorus (purity 99.9) The particles were prepared in the same manner as in Example 1 except that the amount of%) was changed to 0.5 g, to obtain silicon alloy particles.
(粒子の被覆)
実施例1と同様にして、シリコン合金粒子の表面を被覆し、単分子膜で被覆されたシリコン合金粒子を得た。
(Coating of particles)
The surface of the silicon alloy particles was coated in the same manner as in Example 1 to obtain silicon alloy particles coated with a monomolecular film.
(焼結)
実施例1と同様にして、単分子膜被覆が施されたシリコン合金粒子を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 1, the silicon alloy particles coated with the monomolecular film were sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、粉砕前のシリコン合金の98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of that of the silicon alloy before grinding. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.2×105S/mであり、熱伝導率は、4.2W/m・Kであった。焼結体のゼーベック係数(−82.3μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として3.1であった。また、527℃における熱電性能指数ZTは0.54であった。 The electric conductivity at 27 ° C. of the sintered body was 1.2 × 10 5 S / m, and the thermal conductivity was 4.2 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (-82.3 μV / K) of the sintered body, and was 3.1 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.54.
[p型半導体焼結体]
<実施例7>
(シリコン粒子の調製)
単体シリコン(純度99.99%以上)28g及び単体ホウ素(純度99.9%)0.5gを、アーク溶解装置によりアルゴン雰囲気下で融解し、その後冷却した。冷却により得られた塊状物を転動して再び融解して冷却した。この融解及び冷却を計4サイクル繰り返し、母材となるドーパント入りシリコン材を得た。このシリコン材を、ハンマークラッシャー及び遊星ボールミルを利用して、45μm以下に粗粉砕した。さらに、ビーズミルを用いて、D90が150nm程度となるまで粉砕した。このとき、媒体としてイソプロピルアルコールを用い、ビーズとして0.05mm径のジルコニアビーズを使用した。得られたスラリーからイソプロピルアルコールを減圧して除去し、さらに乾燥してシリコン粒子を得た。
[P-type semiconductor sintered body]
Example 7
(Preparation of silicon particles)
28 g of elemental silicon (purity 99.99% or more) and 0.5 g of elemental boron (purity 99.9%) were melted in an argon atmosphere using an arc melting apparatus, and then cooled. The mass obtained by cooling was rolled again to melt and cool. The melting and cooling were repeated a total of four cycles to obtain a dopant-containing silicon material as a base material. This silicon material was roughly crushed to 45 μm or less using a hammer crusher and a planetary ball mill. Furthermore, it grind | pulverized until D90 becomes about 150 nm using the bead mill. At this time, isopropyl alcohol was used as a medium, and zirconia beads of 0.05 mm in diameter were used as beads. From the resulting slurry, isopropyl alcohol was removed under reduced pressure and further dried to obtain silicon particles.
(粒子の被覆)
得られたシリコン粒子をヘプタンに分散し、シリコン粒子5.0gに対してデカボラン0.5gを加えた混合物を上記のビーズミルに投入し、混合処理を300分間行った。その後、ヘプタンを減圧除去し、さらに乾燥して単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
The obtained silicon particles were dispersed in heptane, and a mixture prepared by adding 0.5 g of decaborane to 5.0 g of silicon particles was charged into the above-described bead mill, and the mixing process was performed for 300 minutes. Thereafter, heptane was removed under reduced pressure and further dried to obtain monomolecular film-coated silicon particles.
(焼結)
上記単分子膜被覆が施されたシリコン粉末を、黒鉛製のダイ/パンチ冶具内に装入し、放電プラズマ焼結装置を用いて1200℃まで昇温し、焼結された固体を得た。このとき、加圧圧力を80MPaとし、また昇温速度を50℃/分として行った。得られた焼結体の外表面を粗研磨して黒鉛等に由来する不純物層を除去した。さらに、ダイシングソーを使用して切断し、直方体状のチップを得た。
(Sintering)
The silicon powder coated with the monomolecular film was loaded into a die / punch jig made of graphite and heated to 1200 ° C. using a discharge plasma sintering apparatus to obtain a sintered solid. At this time, the pressurizing pressure was 80 MPa, and the temperature rising rate was 50 ° C./min. The outer surface of the obtained sintered body was roughly polished to remove an impurity layer derived from graphite or the like. Furthermore, it cut | disconnected using the dicing saw and obtained the cube-shaped chip | tip.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. In addition, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon particles having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.1×105S/mであり、熱伝導率は、12.0W/m・Kであった。焼結体のゼーベック係数(89.4μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.30であった。 The electric conductivity at 27 ° C. of the sintered body was 1.1 × 10 5 S / m, and the thermal conductivity was 12.0 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (89.4 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.30.
<実施例8>
(シリコン粒子の調製)
実施例7と同様にして、シリコン粒子を調製した。
Example 8
(Preparation of silicon particles)
Silicon particles were prepared in the same manner as Example 7.
(粒子の被覆)
デカボラン0.5gに代えてトリブチルボラン1.6gを加えた混合物を使用したこと以外は実施例6と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
A monomolecular film-coated silicon particle was obtained in the same manner as in Example 6 except that a mixture of 1.6 g of tributylborane instead of 0.5 g of decaborane was used.
(焼結)
実施例7と同様にして、単分子膜被覆が施されたシリコン粒子を焼結し、焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 7, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. In addition, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon particles having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.0×105S/mであり、熱伝導率は、11.5W/m・Kであった。焼結体のゼーベック係数(93.9μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.1であった。また、527℃における熱電性能指数ZTは0.31であった。 The electric conductivity at 27 ° C. of the sintered body was 1.0 × 10 5 S / m, and the thermal conductivity was 11.5 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (93.9 μV / K) of the sintered body, and was 2.1 based on [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.31.
<実施例9>
(シリコン粒子の調製)
実施例7と同様にして、シリコン粒子を調製した。
Example 9
(Preparation of silicon particles)
Silicon particles were prepared in the same manner as Example 7.
(粒子の被覆)
デカボラン0.5gに代えてトリエチルボレート1.0gを加えた混合物を使用したこと以外は実施例7と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
A monomolecular film-coated silicon particle was obtained in the same manner as in Example 7 except that a mixture in which 1.0 g of triethyl borate was added instead of 0.5 g of decaborane was used.
(焼結)
実施例7と同様にして、上記単分子膜被覆が施されたシリコン粒子を焼結し、焼結体体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 7, the silicon particles coated with the monomolecular film were sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均100nmのシリコン粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon particles of an average of 100 nm were densely bonded was observed.
焼結体の27℃における電気伝導度は1.1×105S/mであり、熱伝導率は、12.5W/m・Kであった。焼結体のゼーベック係数(89.2μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.30であった。 The electric conductivity at 27 ° C. of the sintered body was 1.1 × 10 5 S / m, and the thermal conductivity was 12.5 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (89.2 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.30.
<実施例10>
(シリコン粒子の調製)
単体ホウ素(純度99.9%)0.5gに代えて、単体ホウ素(純度99.9%)0.5g及び単体ガリウム(純度99.99%以上)3.5gを用いたこと以外は実施例7と同様にして、シリコン粒子を調製した。
Example 10
(Preparation of silicon particles)
Example except that 0.5 g of single boron (purity 99.9%) and 3.5 g of single gallium (purity 99.99% or higher) were used instead of 0.5 g of single boron (purity 99.9%) Silicon particles were prepared in the same manner as 7).
(粒子の被覆)
実施例7と同様にして、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
In the same manner as in Example 7, silicon particles coated with a monomolecular film were obtained.
(焼結)
実施例7と同様にして、単分子膜被覆が施されたシリコン粉末を焼結して焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 7, the silicon powder coated with the monomolecular film was sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。 The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.2×105S/mであり、熱伝導率は、9.0W/m・Kであった。焼結体のゼーベック係数(86.6μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.5であった。また、527℃における熱電性能指数ZTは0.31であった。 The electrical conductivity at 27 ° C. of the sintered body was 1.2 × 10 5 S / m, and the thermal conductivity was 9.0 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (86.6 μV / K) of the sintered body, and was 2.5 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.31.
<実施例11>
(シリコン粒子の調製)
モノシラン(SiH4、純度99.9%)100モル当量とジボラン(B2H4、純度99.9%)3モル当量を原料とし、アルゴン/水素混合気を通じてマイクロ波プラズマ反応器により反応させてナノ粒子を合成し、インラインフィルタで捕集した。シリコンナノ粒子が、平均粒径150nm程度の凝集体として得られ、その結晶子の平均径は10nmであった。
Example 11
(Preparation of silicon particles)
Using 100 molar equivalents of monosilane (SiH 4 , purity 99.9%) and 3 molar equivalents of diborane (B 2 H 4 , purity 99.9%) as raw materials, they are reacted in a microwave plasma reactor through an argon / hydrogen mixture The nanoparticles were synthesized and collected by an in-line filter. Silicon nanoparticles were obtained as an aggregate having an average particle diameter of about 150 nm, and the average diameter of the crystallites was 10 nm.
(粒子の被覆)
実施例7と同様に処理して、単分子膜で被覆されたシリコン粒子を得た。
(Coating of particles)
The same treatment as in Example 7 was carried out to obtain monomolecular film-coated silicon particles.
(焼結)
実施例7と同様にして、単分子膜被覆が施されたシリコン粉末を焼結し、焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 7, the silicon powder coated with the monomolecular film was sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、純粋なシリコンの98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of pure silicon. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon crystal grains having an average particle diameter of 100 nm were closely joined was observed.
焼結体の27℃における電気伝導度は1.0×105S/mであり、熱伝導率は、8.8W/m・Kであった。焼結体のゼーベック係数(89.0μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として2.3であった。また、527℃における熱電性能指数ZTは0.30であった。 The electric conductivity at 27 ° C. of the sintered body was 1.0 × 10 5 S / m, and the thermal conductivity was 8.8 W / m · K. The dopant concentration was calculated based on the Seebeck coefficient (89.0 μV / K) of the sintered body, and was 2.3 as a unit of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.30.
<実施例12>
(シリコン合金粒子の調製)
単体シリコン(純度99.99%以上)28gに代えて、単体シリコン(純度99.99%以上)28g及び単体ゲルマニウム(純度99.99%以上)3.0gを使用したこと以外は実施例7と同様にして粒子を調製し、シリコン合金粒子を得た。
Example 12
(Preparation of silicon alloy particles)
Example 7 and Example 7 except that 28 g of single silicon (purity 99.99% or higher) and 3.0 g of single germanium (purity 99.99% or higher) were used instead of 28 g of single silicon (purity 99.99% or higher) Particles were similarly prepared to obtain silicon alloy particles.
(粒子の被覆)
実施例7と同様にして、単分子膜被覆がされたシリコン合金粒子を得た。
(Coating of particles)
In the same manner as in Example 7, monomolecular film-coated silicon alloy particles were obtained.
(焼結)
実施例7と同様にして、上記単分子膜被覆が施されたシリコン粉末を焼結し、焼結体を得て、さらに直方体状のチップを得た。
(Sintering)
In the same manner as in Example 7, the silicon powder coated with the monomolecular film was sintered to obtain a sintered body, and a rectangular parallelepiped chip was further obtained.
(構造及び特性)
アルキメデス法で測定した焼結体の密度は、粉砕前のシリコン合金の98.5%であった。また、焼結体の断面を透過型電子顕微鏡(TEM)で観察したところ、平均粒径100nmのシリコン合金結晶粒が密に接合した構造が観察された。
(Structure and characteristics)
The density of the sintered body measured by the Archimedes method was 98.5% of that of the silicon alloy before grinding. Further, when a cross section of the sintered body was observed by a transmission electron microscope (TEM), a structure in which silicon alloy crystal grains having an average particle diameter of 100 nm were densely bonded was observed.
焼結体の27℃における電気伝導度は1.0×105S/mであり、熱伝導率は、4.5W/m・Kであった。焼結体のゼーベック係数(81.2μV/K)に基づきドーパント濃度を算出したところ、[1020原子数/cm3]を単位として3.3であった。また、527℃における熱電性能指数ZTは0.41であった。 The electric conductivity at 27 ° C. of the sintered body was 1.0 × 10 5 S / m, and the thermal conductivity was 4.5 W / m · K. When the dopant concentration was calculated based on the Seebeck coefficient (81.2 μV / K) of the sintered body, it was 3.3 in units of [10 20 atoms / cm 3 ]. The thermoelectric figure of merit ZT at 527 ° C. was 0.41.
Claims (10)
前記多結晶体は、シリコン、又はシリコン合金を含み、
前記多結晶体を構成する結晶粒の平均粒径が1μm以下であり、
電気伝導率が10,000S/m以上である、半導体焼結体。 A semiconductor sintered body containing a polycrystalline body,
The polycrystalline body includes silicon or a silicon alloy,
The average grain size of crystal grains constituting the polycrystal is 1 μm or less,
The semiconductor sintered compact whose electrical conductivity is 10,000 S / m or more.
前記粒子の表面に、ドーパント元素を含む有機化合物の被膜を形成する被膜形成ステップと、
前記被膜が表面に形成された粒子を焼結して、半導体焼結体を得る焼結ステップと
を含む、半導体焼結体の製造方法。 Preparing a particle comprising silicon or a silicon alloy and having an average particle size of 1 μm or less;
Forming a film of an organic compound containing a dopant element on the surface of the particle;
And sintering the particles having the film formed on the surface to obtain a semiconductor sintered body.
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